Forsterite ceramic bodies



A. G. PINCUS FORSTERITE CERAMIC BODIES Nov; l0, 1959 Filed Nov. 10, 1955 Nov. l0, 1959 A. G. PlNcus 2,912,340

FoRsTERITE CERAMIC BODIES Filed Nov. 10, 1955 2 Sheets-Sheet 2 l /l/ex/ls 6. Pincus,

United States Patent() s claims. (cl. s-62) This invention relates to ceramic bodies having the mineral forsterite as the predominant constituent and, more particularly, to such ceramic bodies which are particularly suited for use in the manufacture of composite structures comprising ceramic bodies bonded to metallic bodies of a metal such as titanium.

In the manufacture of evacuated electronic'zapparatus such as vacuum tubes, increasing use is being m'ade'of the metal titanium for structural elements as well as heating and other emission elements. As is well known, the ability of titanium and zirconium to combine with reactive gases at elevated temperatures has been used in the manufacture of electronic tubes to remove small residual amounts of such gases in an operation commonly referred to as gettering In the past, howeverl gettering has usually been accomplished by heating a small quantity of a reactive metal such as titanium in the evacuated envelope of the apparatus either immediately after the manufacture iscomplete or just before it is put in service. This has usually been a single gettering operation, the titanium element Vbeing exhausted or otherwise rendered inactive after this single operation.v With the recent advent of a more plentiful and relatively inexpensive supply of substantially pure titanium, it has become economically feasible to employ titanium metal for structural elements in electronic tube construction in order that the gettering operation may extend over the life span of the tube and thereby prolong its gas-free life. In order to simplify tube construction, it is desirable to extend these titanium elements through the ceramic portions of the envelope to form electricalv contact with the power source. In a construction of this type it is necessary to provide a vacuumtight joint between the emerging titaniummetal element and the contacting ceramic portions of the envelope which also acts as an electricalinsulator therefor. In use the envelope including the ceramic portions and the elements contained therein become heated and, of course, expand. Since apparatus of this type is usually used in an intermittent fashion, periods during which the temperature of the apparatus may reach as high as 70D-900 C., are alternated with periods during which the temperature of the apparatus may drop to room temperature or lower. Further, under the conditions of operation recited above, the

ceramic must have a power factor of less than 0.002`

particularly in the frequency range ,of 101 cycles, be free of gas evolving constituents, be impermeable to gases, have high electrical resistivity, for example, and be capable of forming a strong vacuum-tight permanent bond :With titanium,

- the past have fallen into two main'categories.

2,912,340 Patented Nov.- 10, 1959 1n one or more of the previously recited requirements.`

In particular, diicnlty has been experienced in forming a strong vacuum-tight permanent bond with titaniumtube structures because of the difference in the coeilicients of thermal expansion or contraction of the, ceramic and titanium. In general, attempts to produce such a jointin A In the first, a sof solder hasbeen used where the operating teniperature' would permit. 'In' this type of construction' the soft solder material flows plastically to relieve stresses arising from differences in expansion and contraction of 'the metal and the ceramic.l Its disadvantages are that higher operating temperatures may not be used and, further, maximum bake-out temperatures are limited.VV Inl the second category, hard solders having a higher melt- V ing point have been used to permit operation at higherl temperatures. In this case, diiculty is experienced with ceramic failure. Attempts to substitute a ceramic having' a suciently high mechanical strength to withstand the thermally induced stresses have not solved the problem in electronic apparatus, principally because these ceramics have not been capableof forming a strong vacuum-tight permanent bond with titanium.

I have discoveredthat ceramic bodies having forsten'te as the predominant mineral constituent, the particular composition. of which will be disclosed in more detail later, have thermal expansion and contraction charac-A teristics matching those of Vcommercial *titanium* metal, that bodies having'thisV composition may be manufactured to be free of gas-evolving constituents, have excellent dielectric properties in the frequency range of 1010 cycles and are capable of forming strong, vacuum-tight permanent bonds and composite structures with titanium metal.

It` is,.the1 'evfo,re, a,pri ncipal,object of my invention to provide a ceramic body having a thermal coeicient of expansion substantially, yidentical to commercial grade titanium metal. -j 'y l v Further, an object of my invention is the Iprovision of a ceramic body having a thermal coeicient of expansion substantiallyidentical to commercial grade titanium metal which additionally has desirable dielectric properties at 10lo cycles, is free of gas-evolving constituents, and is capable of forming strong, vacuum-tightpermanent bonds with titanium.

A still further object of my invention is the provision of a composite body comprising metallic titanium permanently bonded to a ceramic body having an average coefcient of thermal expansion of between 9.4 and 10.4 l0-6 centimeter per centimeter per C. in the temperature range of 25 to 700 C.

My invention will be better understood from the following description taken in connection with the accompanying drawing-and its scope will be-.pointed'out in the appended claims. v

Fig. 1 is a portion of the ternary phase equilibrium diagram of SiO2 -MgO-Al2O3 upon which is shown the Figs. 3 to 5 are graphical representations of the linear contraction characteristics of ceramics having compositions shown in Fig. 1 compared with titanium.

The triangular graph illustrated in Fig. 1 is a portion of the ternary phase equilibrium diagram of the MgO-Al2O3-Si02 system in which the compositions 0f the ceramics of my invention and others of similar composition are shown for purposes of comparison. As will be apparent from inspection, the area of the SiOZ-MgO-AlgOa diagram shown in Fig. 1 illustrates a range of compositions containing from to 75 weight percent SiO2, 0 to 5t) weight percent A1203 and 25 to 75 weight ypercent MgO.

The forsterite ceramic bodies of my invention provide materials closely matching titanium .in thermal expansion, have a lsurprisingly broad firing range for compositions with so few constituents and higher strength than prior art forsterites when sealed to titanium. Preferably, these bodies have a composition located within the forsteritespinel-cordierite coexistence triangle shown in Fig. 1 in broken lines ABC and for best results avoid protoenstatite formation and free MgO. These bodies are composed of forsterite and glass, with the appearance of spinel and then cordierite depending on rate of cooling or on a subsequent anneal around 1G00o C. Preferably, these ceramics may be produced within the limits enclosed by the triangle formed by the straight lines connecting points D, E, F illustrated in Fig. 1 determined by the three compositions with vitrification (vacuum tightness) over a practical firing range of temperatures assisted by the Fe2O3, TiO2, Zr02, CaO, and NaKO, normally present as impurities even in the purest grades of raw materials. These impurities, however, should not exceed a total amount of about 4 percent by weight of the tired ceramic, and preferably should not exceed 2 percent, particularly if the ceramic is to be used in vacuum tube applications.

A number of ceramic bodies having compositions within and near the above-recited limits were formed and tired at varying temperatures and times. The dielectric properties, thermal contraction characteristics and other physical properties were observed and measured and will be subsequently listed and compared.

In the preparation of these bodies, two general procedures were followed. Certain compositions were prepared from naturally occurring raw materials, i.e., talc and clay with added magnesium hydroxide while others were prepared from pure oxides, i.e., magnesium carbonate or magnesium hydroxide, which decompose to MgO upon tiring, alumina (99.9 percent A1203) and a commercial potters flint (99.9 percent SiO-2) preferably in a special ultrafine grind. The naturally occurring raw materials, talc and clay, and the magnesium hydroxide had the following representative analyses of the listed constituents in weight percent based upon the weight of the material before tiring. These materials also contained minor amounts of volatile substances such as water and amounts of carbon dioxide (present as carbonatos? which are lost on ignition.

.e TABLE I F actors used in computing analyses or batches TALCS California Montana 59. 6 62. 5 29. 9 30. 2 2. 1 0. 3 0. 9 1. 5 n.d. tr 0. 9 tr 0. 5 0.2

CLAYS Ky. Ball Florida Clay Kaolin si. 7 47. o 31. 2 36. 8 1. 2 D. 5 1. 7 0. 2 O. 5 0. 2 0. 2 0. 1 O. 9 0. 2

MgCO:

'Percent Loss on Ignition 57.4 l g 42,. 6 Mg(0H)i Loss on Ignition M gO BaO Oa Loss on Ignition 2 2. l BaO 77. 9

In the preparation of compositions from these materials, the above analyses of these materials were used in pre` paring the bodies as is well known in the art.

Batches of the various compositions were prepared by weighing appropriate amounts of 'the various ingredients into a ball mill containing flint pebbles. A sutiicient amount of water was added to obtain a free owing slip,

the amount of water varying from about 2500 to about 3090 cubic centimeters per kilogram of d ry ingredients. These mixtures were mil-led for about four hours. After milling the mixtures were lfilter p'essed, dried, crushed and pulverized with appropriate apparatus. A-tthis point, a precalcining step may be employed if desired, as wiil. be set forth in greater detail later. The puiverized mixtures which were to be vformed Aby pressing were then mixed with an appropriate amount Yof binder and lubricant, for example, about 7 percent of the weight of the batch of a 1'() percent solution of Ipolyvinyl alcohol in water was thoroughly mixed therewith. The mixtures were again pulverized and were formed `into suitable bodies by conventional pressing operations at about sii'. tons per square inch. The pulvcrized materials which were to be formed by conventional extrusion operations were mixed with a greater amount of the b'nder and lubricant, for example, of 4() percent by we ht of the batch of a 17 percent solution of poiyvinyl alcohol in water was mixed therewith to form a smooth, putty-like mass. lt should be here -noted that other satisfactory materials may be used in place of lthe recited lpolyvinyl alcohol Vsolutions as binder and lubricant. For example, glycerin has been found to function equally well.

The formed bodies were then placed in suitable open vessels upon a suitable substrate contained therein comprising sands consisting of silica, magnesia, aluminaor zirconia and tired in an air atmosphere in an electrical resistance furnace.

Among many bodies prepared, batches having the lfollowing nominal compositions will be more specicnll-y disclosed and described subsequently in the disclosure.

e listed Density which had been re tested by conproperties were 'LLF.

.6... Hours ATABLE Fired o?" I ILLLLLLLLLLLLLLI,

LlflrLlylrLlvtMLlilrLllyLLlylyl.

l l i i, i f l LLLLI'LLLILLLLLLLLL1# TABLE VI Hours Pecent Percent Percent Percent B101 MgO A130: BaO

TABLE111'.. Nominal corrpasitions.'

Batch No.

1 Batches 12-17 nianuiactured from pure materials, Le., alumina, 20 5 ques and the following Fired Dielectric test specimens of certain of theabov compositions were prepared from disks 50 pressed and fired as noted in Table V we ventional techni determined.

computed compositions, d upon specimen bodies. the close agreement-bepositions and that found upon` performe ustrates TABLE IV Comparisons of actual and computed analyses tion of these bodies with their chemical analyses were The lfollowing table ill tween the computed com actual analyses in weight percent.

As shownrabove, the dielectric properties of the sei/eral at the three centimeter the bodies were cooled and inspected for porosity, cracks and surface defects, such as blisters or pimples, and unf desirable reaction with the placing sand. 75 forsterite bodies were measured wavelength. The values for dielectric constant (K) and power factor (P.F., expressed as tan 5X 104) were measured from specimens of the respective bodies measuring 1.000 i0.001 inch by 0.500 *0.001 inch by quarter Wave thickness employing measuring procedures and apparatus well known in the art. For a detailed description of such apparatus and procedures, see Dielectric Properties of Glasses at Ultra-High Frequencies and Their Relation to Composition, Navias et al., I. Am. Ceram. Soc., 15, 234-251 (1932).

In materials of this type, it is desirable to maintain low loss factor, L.F. in Table VI, which is a product of the power factor multiplied by the dielectric constant for a given material. Loss factors for materials for this ty'pe should be less than about 0.01 and preferably as low as possible. In view of the magnitude of the numbers involved, it is obvious that a comparatively low dielectric constant is to be greatly desired in these bodies. To compare, a test specimen from the barium-containing material of batch l0 was tired at 1275 C. and the dielectric constant measured at a wavelength of three centimeters was found to be 6.3, a value which is considerably higher than that of comparative forsterite ceramics of my invention, for example bodies from batches 3, 4, 5, 6 (red at 1400 C.), 7 and 8 as seen in the preceding Table VI.

I have found that the power factor of these materials is more directly related to composition. In general, it may be said for compositions in the area outlined by the triangle D, E, F in Fig. l that the power factor of these bodies tends to increase with an increase in alumina content. Consequently better dielectric properties, particularly dielectric constant, are to be found in ceramic bodies having compositions located toward and within the lefthand portion of the triangular area D-E-F shown in Fig. 1, and in particular within the triangular area determined by the straight lines connecting points D, G, H of Fig. l, in which point G is a composition containing about 41 weight percent SiO-2, 44 weight percent MgO and l5 weight percent A1203, and point H is a composition containing about 34.5 weight percent SiO2, 50.5 weight percent MgO and 15 weight percent Al2O3. More specically, bodies prepared from batches S, 13, 14, l5 and 16 have excellent mechanical and electrical properties.

One of the contemplated uses of the forsterite ceramics of my invention is as envelope elements of Vacuum tubes. An example of such an electronic tube is schematically shown in vertical section in Fig. 2 in which members 30, 31 and 32 are formed disk-like elements of metallic titanium or zirconium or alloys thereof. Members 33 and 34 comprise toroidal elements having central open portions 35 and 36.

Member 30 in this exemplary tube comprises an anode portion 37. Member 31 is a washer-like element having a central aperture 38 across which is provided a screenlike grid member 39 which is in electrical contact with member 31.

Member 32 comprises a cathode portion 40 which may be provided with an electrical resistance heater element 41 as shown.

The several elements 30, 31, 32, 33 and 34 are assembled into an enclosed tube body or envelope as shown. The metallic members 30, 31 and 32 are sealed to the ceramic members 33 and 34 by any known satisfactory soldering or brazing technique such as, for example, as disclosed in U.S. Letters Patent 2,570,248, Kelley, at their abutting surfaces after the interior formed by the communicating spaces 35, 36 and 38 has been evacuated of atmospheric and other gases and subjected to a bakeout as is well known in the electronic tube art. Electrical connections may be provided for the anode, grid and cathode elements of such a tube through the exposed portions of members 30, 31 and 32, respectively.

It is desired to fabricate members, such as elements 30, 31 and 32, from relatively pure titanium for reasons stated previously. In view of the thermal cycling to which such tubes are subjected during operation, it is necessary that the ceramic bodies from which elements such as 33 and 34 are formed have thermal expansion and contraction characteristics closely approaching those characteristics of titanium in order that rupture of the ceramic or of the seal between the metallic and ceramic bodies not be broken, thereby destroying the tube. Further, the ceramic bodies must have low dielectric losses, high resistivity and be vacuum tight. Obviously porosity of these ceramics is a characteristic to be avoided. Further, the bulk density of these materials should be maintained as high as practicable. In addition, the ceramic bodies should be free from gas evolving constituents over the operating temperature range and in particular be free from constituents which may evolve substances which progressively poison or otherwise deleteriously affect the emission characteristics of the cathode during operation of the tube.

The thermal expansion characteristics of ceramic bodies of my invention were measured and compared to the thermal expansion characteristics of metallic titanium and to ceramic bodies having similar compositions.

TABLE VII Fired Thermal Expansion CoeirientXiO Batch No.

Temp., Hours 25-300 25-500 25-700 25-1,000

C. C. C C. C.

Titanium 8. 5 9.2 9. 8 10. 3 1 1 7.6 7. 4 8.2 4 1.1 1. 7 3. 7 5. 6

From the foregoing, it may be readily seen that the bodies from ibatches 3, 5, 6, 7 and 8 whose compositions are within the triangular area D-Ef-F in Fig. 1 have thermal expansion and contraction coeflicients very close to the corresponding coefficients for titanium, while the bodies from batches 1, 2 and l0 do not have such close agreement thereto. It will be seen that body 11 which has a composition outside the triangular area D-E-F has very good expansion characteristics.

The body from batch 11 has, however, shown itself to oe undesirable in that during the sealing of tubes similar to the exemplary tube of Fig. 2, the metallic titanium elements and the ceramic members exhibited a strong reaction resulting in weak bonds, discoloration of the ceramic at sealing surfaces, leaks and blackening of the interior of the tubes resulting in inferior tube performance at elevated temperatures encountered during operating conditions. This undesirable behavior has been attributed to the high barium content of the ceramic. It has been found that the BaO content of the ceramics of my invention should not exceed l percent lby weight in order to eliminate these diiiculties.

In Fig. 3 a graphical comparison is made of the thermal contraction curve of ceramic bodies having the composition of batch 8 fired at different temperatures and times with that for titanium. The solid line curve I represents the linear thermal contraction characteristics of titanium measured in centimeters per centimeter X106 as itis cooled from 1000 C. to room temperature. In the determination of the thermal coeiicients of expansion of these materials and titanium, the cooling was accomplished at the normal, power-off rate of the furnace or slightly delayed at the first stages of cooling. The dotted line curve identified by II represents the linear thermal contraction characteristics of a ceramic body of the composition of batch 8 which had been air-fired at 1400 C.

The curves in Fig. 4 illustrate the linear thermallconcom.

traction characteristics of a ceramic body having the position of batch 3 fired at 1375 C. for 1 hour compared to the contraction characteristics of titanium measured in centimeters per centimeter 10-6 whileV being cooled from 1000 C. to room temperature. The solid line curve identified by .V illustrates the linear thermal contraction characteristics of titanium while the dotted line curve identified by VI is illustrative of the behavior of a ceramic body of the composition of batch 3 under identical condi' tions.v Solid line curve VII illustrates the linear thermal contraction characteristics of the same specimen measured 68 days later. "1' A v v l v The curves in Fig. 5 illustrate the linear thermal contraction characteristics of a body having the composition of batch l and similar characteristics of a body having the composition of batch 2. Theupper curve VIII shows the thermal contraction behavior of a body, batch 1, fired at 1350 C. for one hour. As previously shown in Table VIII, this material has coefficients of thermal contraction for ,the several ranges listed which are considerably lower than titanium and further, the sharp discontinuity eX- hibited between 500 and 600 C. renders it unsuitable vfor the manufacture of bonded compositeceramic and titanium bodies for use under temperatures which cyclically vary from room temperature to 700 C. or higher.

The curve IX illustrates the linear thermal contraction characteristics of a body having the composition of batch 2. The well-defined knee in this curve clearly shows this ceramic to be unsuitable for bonding to titanium for the previously stated purposes and reasons.

As stated previously, a number of bodies having compositions within the triangular area D-E-F shown in Fig. 1 were prepared from pure materialsjjBy using the previously described pure magnesium carbonate or magnesium hydroxide, alumina and potters flint, ceramic bodies containing small and controllable amounts of impurities may be produced. Further, by thus controlling the impurities in the composition, better control may b e achieved of such properties as density, dimensional stability vduring firing, dielectric properties, impermeability to gases and freedom from gas evolving constituents. In order that ceramic bodies having these desirable characteristics may be consistently prepared, it has been found desirable to precalcine the constituents prior to the forming and firing operations.' Itjshould be noted lthat precalciuation may be advantageously utilized with the naturally occurring raw materials as well as with the pure materials. I

A mixture of substantially pure (commercially pure) magnesium carbonate, alumina (99.9% A1203) and finely ground commercial potters v.iiint y (99.9% SiO3 was ground in a ball mill forfour hours with sutiicient water corresponding Vto that of batch 6 and will be hereinafter referred to as batch 6. Bodies having this composition made from the -precalcined pure.4 materials were red at 1400 C. for one hour andrl450 C. for one hour and found to be vacuum tight. Upon comparison of the properties of bodies 6 and 6' as shown in the following to obtain a free flowing slip. The ground batch was filter table'it will be seen that several advantages may be attained `by theuse of precalcined pureraw materials.

TABLE VIII Fired Barchi K RF. LF. Density Y Temp., Hours o.

6 1, 400 1 5.4 0. 00077 0. 0041 2.532 1, 450 1 5. 5 00080 0. 0044 2. 668 6, 1, 400 1 s. s 0. 0010 0. 0003y a. 000 1, 450 l 6. 1 0.001'3 0. 0079 2. 904

A considerable improvement in dimensional changes during firing, a Yhigher density and a coeicient of thermal like elements of batch 6 composition were found tofhavel a firing shrinkage of about 19.5 percent-in diameter and 30.4 percent in height when fired at 1400 C. 'for one hour. Identical elements of batch 6 composition were found to have a. firing shrinkage. of about 15.8 percent in diameter and 13.5 percent in height under the same .firing conditions. Further, the coefiicient of thermal contraction for the body having the composition of batch 6 for 25 C. to .300 'C. is 8.7 X10*6 cm. per cm. per C., for25 to 500 C. is 9.8 10 cm. per cm. per C., for 25 C. to,700 C. is l0.4 l0*6=cm. per cm. per C. and,for:25 C. tov 1000" ,C. is.f1l.3 106 cm. per cm. per ,C. It will be seen,.however, vthat the bodies made from the precalcined material have a somewhat higher dielectric constant. However, the power factors are low enough so that the loss factor is acceptably low.-

, Precalcination may be preferably accomplished in the following manner, if desired. A mixture of magnesium carbonate or magnesium hydroxide and potters flint las previouslyA described may be prepared containing suffic ient magnesium carbonate orI hydroxide and SiO2 to form the stoichiometric ratio of Qforsterite, 2MgO-SiO2. Upon firing with the consequent decomposition of the magnesium carbonate or hydroxide to magnesium oxide a composition of about 57.1 percent MgO and about 42.9 percent SiOz will be achieved. This composition corresponds to point B in Fig. 1 and is substantially pure forsterite. The forsterite composition so produced may then be pulverized and mixedpwith appropriate amounts of magnesium hydroxide, pure alumina and SiOZ or potters flint to achieve any desired composition within triangular area D-E*F upon subsequent-firing. Bodies having excellent propertiesmay be conveniently formed by firing mixtures of the alumina alone. These bodies will have compositions lying within the lower triangular area D-G H providing, at least 1.0 weight percent and not more than l5 weight percent A1203 isadded to the forsterite composition. Greater homogeneity may be achieved in bodies prepared in this manner in that a maximum amount of forsterite is present in bodies prepared in this manner. Another advantage of this method of preparation is that higher calcining temperatures are practical in that there is a smaller degree of sintering rendering the calcined particles easier to crush. Y

, In order to'produce ceramic bodies according to my invention it is necessary that the composition .be main forsteritev composition with tained within the limits of from about 32.5 to 46 weight percent Si02, 33 to 56.5 percent MgO and 1 to 21 percent A1203, a compositional range included within triangular area D-E-F of Fig. 1, and preferably from 34.5 to 42.5 Weight percent Si02, 44 to 56.5 percent Mg0 and 1 to 15 percent A1203, a compositional range iucluded within triangular area D-G-H of Fig. 1. l have found that ceramics having compositions outside the area defined by the triangular area D-E-F in Fig. 1 and particularly those having compositions lying in areas in the figure above the line D-E are not stable, i.e., over a period of time, for example, the coefficient of thermal contraction for such bodies has a tendency to change. Further, as shown by the previously disclosed properties, the dielectric properties tend to deteriorate as the alumina content increases and compositions such as that of batch 9 containing about 20 percent or more alumina have a very narrow tiring range and tend to be porous. Ceramic bodies containing Mg in excess of those compositions lying along line D-F are undesirable because of the diculty in obtaining vitritication upon tiring. For example, vacuum tight bodies having the compositions of batches and 16 were obtained when tired at temperatures betwen 1450 and 1600 C., while bodies prepared from batch 17 were tired at temperatures as high as 1700 C. without causing vitritication. These non-vitried bodies had very low mechanical strength and were porous.

The ceramic bodies having compositions within area D-G-H of Fig. 1 were characterized by broader tiring ranges to produce vacuum tight bodies, greater stability, coefficients of thermal expansion and contraction very similar to metallic titanium and freedom from gas evolving constituents. in addition, these ceramic bodies possess highly desirable dielectric properties and may be advantageously utilized as disclosed in the manucture of vacuum tubes such as shown in Fig. 2 in addition to other electrical apparatus such as magnetrons, traveling wave tubes, ionization gages, power resistors, capacitors and other apparatus where the unique properties which these ceramics possess may be necessary.

Composite bodies consisting essentially of formed and fired bodies of the ceramics of my invention permanently bonded to titanium bodies have successfully withstood many cycles of temperature variation between room temperature and temperatures of the order of 700 C. for long periods of time. Furthermore, the ceramicsv of my invention have been incorporated into vacuum tubes similar in construction to that illustrated in Fig. 2 in which formed and tired ceramic bodies of my invention were permanently bonded to titanium elements to form tube envelopes. These tubes were successfully operated for long periods of time under conditions which included thermal cycling between room temperature and 700 C. without developing leaks caused by porosity in the ceramic or mechanical fracture thereof. Further, these ceramic tube elements showed little or no tendency to emit gases.

From the foregoing, it will be seen that l have provided a ceramic material from which strong, stable bodies may be made which have a thermal coefhcient of expansion substantially identical to commercial grade titanium metal, which have useful dielectric properties at 1010 cycles, are free of gas-evolving constituents and are capable of forming strong vacuum-tight permanent bonds with titanium. While 1 have disclosed particular utility for these ceramics in the manufacture of electronic apparatus, particularly vacuum tube applications, it is to be understood that these particular uses are exemplary only and many other applications will occur to one skilled in the art, for example, in bushings or terminals. I, therefore, do not desire or intend that my invention shall be limited to these several disclosed applications and only intend to limit my invention to the subject matter of the appended claims.

What I claim as new and desire to secure by Letters Patent of the United States is:

1. A forsterite ceramic body consisting essentially of a vitrified mixture of Si02, MgO and A1203 having compositional limits within the triangular area of the ternary phase equilibrium diagram of the Si02, MgO and A1203 system bounded by straight lines connecting compositions consisting of about (1) 42.5 Weight percent Si02, 56.5 weight percent MgO, and 1.0 weight percent A1203; (2) 4] weight percent Si02, 44 Weight percent MgO and 15 tr/eight percent A1203; and (3) 34.5 weight percent Si02, 50.5 weight percent MgO and 15 weight percent A1203, said body being vitriiied to the extent that it is vacuum tight and free from continuous porosity and not to the ext-ent that surface defects or cracks are produced, and said body containing crystalline forsterite as the major mineral constituent and containing spinel and glass as minor mineral constituents and being substantially free from protoenstatite and free magnesium oxide and having an average coefficient of thermal expansion between 25 C. and 700 C. of about 94x10-6 centimeter per centimeter per C. to about 10.4 106 centimeter per centimeter per thermal expansion and contraction.

2. A forsterite ceramic body consisting essentiallyof a vitried mixture of Si02, MgO and A1203 having compositional limits within the triangular area of the ternary phase equilibrium diagram of the S102, MgO and A1203 system bounded by straight lines connecting compositions consisting of about (1) 42.5 weight percent SiO2, 56.5

eight percent MgO, and 1.0 weight percent A1203; (2) 41 weight per cent Si02, 44 weight percent MgO and 15 weight percent A1203; and (3) 34.5 weight percent Si02, 50.5 weight percent MgO and 15 weight percent A1203, said body containing less than a total of 4 weight percent of impurities consisting of oxides of iron, titanium, Zirconium, calcium, sodium and potassium and less than about 1 weight percent of barium oxide, the body being vitried to the extent that it is vacuum tight and free from continuous porosity and not to the extent that surface defects or cracks are, produced, and said body containing crystalline forsterite as the major mineral constituent and containing spinel and glass as minor mineral constituents and being substantially free from protoenstatite and free magnesium oxide and having an average coetiicient of thermal expansion between 25 C. and 700 C. of about 9.4 106 centimeter per centimeter per C. to about 10.4 1O-6 centimeter per centimeter per C. and matching metallic titanium in thermal expansion and contraction.

3. A forsterite ceramic body consisting essentially of a vitried mixture of Si02, MgO and A1203 having compositional limits within the triangular area of the ternary phase equilibrium diagram of the Si02, MgO and Al203 system bounded by straight lines connecting compositions consisting of about 1) 42.5 Weight percent Si02, 56.5 weight percent MgO, and 1.0 Weight percent A1203; (2) 41 weight percent Si02, 44 weight percent MgO and 15 Weight percent A1202; and (3) 34.5 weight percent S02, 50.5 weight percent MgO and 15 weight percent A1203, said body containing less than a total of 2 weight percent of impurities consisting of oxides of iron, titanium, zirconium, calcium, sodium and potassium and less than about 1 weight percent of barium oxide, the body being vitried to the extent that it is vacuum tight and free from continuous porosity and not to the extent that surface defects or cracks are produced, and said body containing crystalline forsterite as the major mineral constituent and containing spinel and glass as minor mineral constituents and being substantially free from protoenstatite and free magnesium oxide and having an average coefficient of thermal expansion between 25 C. and 700 C. of about 9.4 105 centimeter per centimeter per C. to about 10.110606 centimeter per centimeter per C. and match- C. and matching metallic titanium ining metallic titanium in thermal expansion and contraction.

4. A forsterite ceramic body consisting essentially of a vitritied mixture of about 40 to 42 weight percent SiO2, to 7 weight percent A1203 and the balance substantially all MgO with less than 2 weight percent of oxides of iron, titanium, zirconium, calcium, sodium and potassium and less than about 1 Weight percent of barium oxide as impurities, said body being vitried to the extent that it is vacuum tight and free from continuous porosity and not to the extent that surface defects or cracks are produced, and said body containing crystalline forsterite as the major mineral constituent and containing spinel and glass as minor mineral constituents and being substantially free from protoenstatite and free magnesium oxide and having an average coelicient of thermal expansion between 25 C. and 700 C. of about 94x106 centimeter per centimeter per C. to about 10.4 106 centimeter per centimeter per C. and matching metallic titanium in thermal expansion and contraction.

5. A forsterite ceramic body consisting essentially of a vitried mixture of about 41.5 to 42.5 weight percent Si02, 2.5 to 3.5 weight percent A1203 and the balance substantially all Mg0 with less than 2 weight percent of oxides of iron, titanium, zirconium, calcium, sodium and potassium and less than about 1 weight percent of barium oxide as impurities, said body being vitried to the eX- tent that it is vacuum tight and free from continuous porosityand not to the extent that surface defects or cracks are produced, and said body containing crystalline forsterite as the major mineral constituent and containing spinel and glass as minor mineral constituents and being substantially free from protoenstatite and free magnesium oxide and having an average coeicient of thermal expansion between 25 C. and 700 C. of about 9.4 106 centimeter per centimeter per C. to about 10.4 103 centimeter per centimeter per C. and matching metallic titanium in thermal expansion and contraction.

6. A forsterite ceramic body consisting essentially of a vitriied mixture of about 39 to 41 weight percent Si02, 9 to 11 weight percent A1203 and the balance substantially all Mg0 with less than a total of 2 weight percent of oxides of iron, titanium, zirconium, calcium, sodium and potassium and less than about 1 weight percent of barium oxide as impurities, said body being vitriiied to the extent that it is vacuum tight and free from contnuous porosity and not to the extent that surface defects or cracks are produced, and said body containing crystalline forsterite as the major mineral constituent and containing spinel and glass as minor mineral constituents and being substantially free from protoenstatite and free magnesium oxide and having an average coeicient of thermal expansion between 25 C. and 700 C. of about 9.4)(106 centimeter per centimeter per C. to about 10.4 10,6 centimeter per centimeter per C. and

Cit

matching metallic titanium in thermal expansion and contraction.

7. A forsterite ceramic body consisting essentially of a vitrified mixture of about 36 to 38 weight percent Si02, 13 to 15 weight percent A1202 and the balance substantially all MgO with less than a total of 2 weight percent nesium oxide and haying an average coelcient of thermal expansion between 25 C. and 700 C. of about 9.4)(108 `centimeter per centimeter per C. to about 10.4 1O8 centimeter per centimeter per C. and matching metallic titanium in thermal expansion and contraction.

8. A forsterite ceramic body consisting essentially of a vitried mixture of about 37 weight percent Si02, about 49 weight percent MgO, and about 14 weight percent A1203, said body being vitried to the extent that it is vacuum tight and free from continuous porosity and not to the extent that surface defects or cracks are produced, and said body containing crystalline forsterite as the major mineral constituent and containing spinel and glass as lminor mineral constituents and being substantially free from protoenstatite and free magnesium oxide and having an average coefficient of thermal expansion between 25 C. and 700 C. of about 9.4 l0s centimeter per centimeter per C. to about 10.4 106 centimeter per centimeter per C. and matching metallic titanium in thermal expansion and contraction.

References Cited in the flle of this patent OTHER REFERENCES 5,198 Cannon Iuiy 24, 1847 2,100,187 Handrek Nov. 23, 1937 2,163,409 Pulfrich June 20, 1939 2,332,343 Rigtcrink Oct. 19, 1943 2,599,184 Lathe June 3, 1952 2,731,355 Skiner June 17, 1956 FOREIGN PATENTSv 456,459 France 1913 OTHER REFERENCES Journal American Ceramic Society, vol. 30, part II of November 1947, pages 79 and 80, Figs. 260-264.

Ternary System Mg0-A1203-Si02, by G. A. Rankin and H. E. Merwin from the American Journal of Science, April 1918 (pp. 301-325). 

1. A FORSTERITE CERAMIC BODY CONSISTING ESSENTIALLY OF A VITRIFIED MIXTURE OF SIO2 MGO AND AL2O3 HAVING COMPOSITIONAL LIMITS WITHIN THE TRIANGULAR AREA OF THE TERNARY PHASE EQUILIBUM DIAGRAM OF THE SIO2 MGO AND AL2O3 SYSTEM BOUNDED BY STRAIGHT LINES CONNECTING COMPOSITIONS CONSISTING OF ABOUT (1) 42.5 WEIGHT PERCENT SIO2, 56.5 WEIGHT PERCENT SIO2 44 WEIGHT PERCENT AL2O2; (2) 41 WEIGHT PERCENT SIO2 44 WEIGHT PERCENT MGO AND 15 WEIGHT PERCENT AL2O2; AND (3) 34.5 WEIGHT PERCENT AL2O 50.5 WEIGHT PERCENT MGO AND 15 WEIGHT PERCENT AL2O3, SAID BODY BEING VITRIFIED TO THE EXTENT THAT IS VACUUM TIGHT AND FREE FROM CONTINUOUS POROSITY AND NOT TO THE EXTENT THAT SURFACE DEFECTS OR CRACKS ARE PRODUCED, AND SAID BODY CONTAINING CRYSTALLINE FORSTERIE AS THE MAJOR MINERAL CONSTITUENTS AND CONTAINING SPINEL AND GLASS AS MINOR MINERAL CONSTITUENTS AND BEING SUBSTANTIALLY FREE FROM PROTENSTATITE AND FREE MAGNESIUM OXIDE AND HAVING AN AVERAGE COEFFICIENT OF THERMAL EXPANSION BETWEEN 25*C. AND 700*C. OF ABOUT 9.4X10-6 CENTIMETER PER CENTIMER PER *C. TO ABOUT 10.4X10-6 CENTIMETER PER CENTIMETER PER *C. AND MATCHING METALLIC TITANIUM IN THERMAL EXPANSION AND CONTRACTION. 